Butene-1 polymer having a high melt flow rate

ABSTRACT

A butene-1 polymer having:
         a) a Melt Flow Rate value of from 20 to less than 100 g/10 min., measured according to ISO 1133 at 190° C. with a load of 2.16 kg;   b) an intrinsic viscosity (IV) measured in tetrahydronaphthalene (THN) at 135° C. equal to lower than 0.95 dl/g;   c) a Mw/Mn value equal to or lower than 3.5 and a lower limit of 1.5;   d) a Mz value of 180,000 g/mol or higher; and   e) optionally, a comonomer content of up to 10% by weight.

FIELD OF THE INVENTION

In general, the present disclosure relates to the field of chemistry. More specifically, the present disclosure relates to polymer chemistry. In particular, the present disclosure relates to a butene-1 polymer as well as films, fibers, hot-melt adhesives, polymer additives, and fluidizers made therefrom.

BACKGROUND OF THE INVENTION

Butene-1 polymers having high melt flow rate have been used in many application fields. In those applications, the utility of the butene-1 polymers is believed due to properties such as chemical inertia, mechanical properties and nontoxicity.

In some instances, the molecular weights and molecular weight distribution of the butene-1 polymer have an effect on the final polymer properties.

SUMMARY OF THE INVENTION

In a general embodiment, the present disclosure provides a butene-1 polymer having:

-   a) a Melt Flow Rate value of from 20 to less than 100 g/10 min.,     alternatively from 25 to 95 g/10 min., alternatively from 30 to 80     g/10 min., measured according to ISO 1133 at 190° C. with a load of     2.16 kg (hereinafter called “MFR”); -   b) an intrinsic viscosity (IV) measured in tetrahydronaphthalene     (THN) at 135° C. equal to lower than 0.95 dl/g, alternatively equal     to lower than 0.90 dl/g, alternatively from 0.75 dl/g to 0.95 dl/g,     alternatively from 0.75 dl/g to 0.90 dl/g; -   c) a Mw/Mn value, where Mw is the weight average molar mass and Mn     is the number average molar mass, both measured by GPC (Gel     Permeation Chromatography), equal to or lower than 3.5,     alternatively equal to or lower than 3, alternatively equal to or     lower than 2.5, the lower limit being of 1.5 for the ranges; -   d) a Mz value of 180,000 g/mol or higher, alternatively of 190,000     g/mol or higher, alternatively from 180,000 to 350,000 g/mol,     alternatively from 190,000 to 300,000 g/mol; and -   e) optionally, a comonomer content of up to 10% by mole,     alternatively up to 8% by mole, alternatively of from 1% to 10% by     mole, alternatively from 1% to 8% by mole.

In some embodiments, the butene-1 polymer is obtained directly in polymerization in the absence of free radical generating agents like peroxides, thereby increasing the MFR value and avoiding the chemical contamination and unpleasant odor which results from the introduction of free radical generating agents.

In some embodiments, the butene-1 polymer is blended with other polyolefins, alternatively propylene polymers. In some embodiments, the butene-1 polymer is used in films, fibers, and hot melt compositions.

DETAILED DESCRIPTION OF THE INVENTION

In some embodiments, the present butene-1 polymer is a homopolymer or a butene-1 copolymer. In some embodiments, the butene-1 copolymer is made from or contains one or more comonomers selected from the group consisting of ethylene and higher alpha-olefins.

In some embodiments, the higher alpha-olefins have the formula CH2═CHR wherein R is methyl or an alkyl radical containing 3 to 8 or 3 to 6 carbon atoms. In some embodiments, the higher alpha-olefins are selected from the group consisting of propylene, hexene-1, and octene-1.

In some embodiments, ethylene is the comonomer.

The present butene-1 polymer has a measurable crystallinity, as demonstrated by the presence, in the Differential Scanning calorimetry (DSC) pattern, of the melting temperature peaks of crystalline butene-1 polymers.

In some embodiments, the present butene-1 polymer shows one or more melting peaks in the second DSC heating scan. In some embodiments, the temperature peak or peaks occurring at temperatures equal to or lower than 100° C., alternatively equal to or lower than 85° C., alternatively from 40° C. to 100° C., alternatively from 45° C. to 85° C. It is believed that such temperature peaks are attributed to the melting point of crystalline form II of the butene-1 polymers (TmII) and the area under the peak (or peaks) is taken as the global melting enthalpy (DH TmII). However, if more than one peak is present, the highest (most intense) peak is taken as TmII.

In some embodiments, global DH TmII values for the present butene-1 polymer are of 25 J/g or less, alternatively from 0.2 to 25 J/g, alternatively from 0.2 to 20 J/g, measured with a scanning speed corresponding to 10° C./min.

In some embodiments, the present butene-1 polymer shows one or more melting peaks occurring at temperatures equal to or lower than 100° C., alternatively equal to or lower than 89° C., alternatively from 30° C. to 100° C., alternatively from 30° C. to 89° C., in a DSC heating scan carried out after aging. It is believed that such temperature peak or peaks are attributed to the melting point of crystalline form I of the butene-1 polymers (TmI) and the area under the peak (or peaks) is taken as the global melting enthalpy (DH TmI). However, if more than one peak is present, the highest (most intense) peak is taken as TmI.

In some embodiments, global DH TmI values for the present butene-1 polymer are of 50 J/g or less, alternatively from 25 to 50 J/g, alternatively from 30 to 50 J/g, measured with a scanning speed corresponding to 10° C./min.

In some embodiments, the present butene-1 polymer has a detectable content of crystalline form III. Crystalline form III is detectable via the X-ray diffraction method described in the Journal of Polymer Science Part B: Polymer Letters Volume 1, Issue 11, pages 587-591, November 1963, or Macromolecules, Vol. 35, No. 7, 2002.

In some embodiments, X-ray crystallinity values for the present butene-1 polymer are from 10% to 45%, alternatively from 15% to 40%. In some embodiments, the present butene-1 polymer has at least one of the following further features:

-   Mw equal to or greater than 90,000 g/mol, alternatively from 90,000     to 200,000 g/mol, alternatively from 100,000 to 180,000 g/mol; -   isotactic pentads (mmmm) measured with ¹³C-NMR operating at 150.91     MHz higher than 90%; alternatively higher than 93%, alternatively     higher than 95%; -   4,1 insertions not detectable using a ¹³C-NMR operating at 150.91     MHz; -   a yellowness index lower than 0; alternatively from 0 to -10,     alternatively from −1 to −9, alternatively from −1 to −5; -   a Shore D value equal to or lower than 50, alternatively equal to or     lower than 45, alternatively from 15 to 50, alternatively from 15 to     45; -   a tensile stress at break, measured according to ISO 527, of from 10     MPa to 45 MPa, alternatively from 15 MPa to 40 MPa; -   a tensile elongation at break, measured according to ISO 527, of     from 400% to 1000%; alternatively from 450% to 700%; -   a glass transition temperature of −18° C. or less, alternatively of     -20° C. or less, wherein the lower limit is −25° C.; -   a density of 0.880 g/cm³ or more, alternatively of 0.885 g/cm³ or     more; wherein the upper limit is of 0.899 g/cm³; -   content of fraction soluble in xylene at 0° C. of 95% by weight or     higher, up to 100% by weight.

In some embodiments, the butene-1 polymer is obtained by polymerizing the monomer(s) in the presence of a metallocene catalyst system obtainable by contacting:

-   a stereorigid metallocene compound; -   an alumoxane or a compound capable of forming an alkyl metallocene     cation; and, optionally, -   an organo aluminum compound.

In some embodiments, the stereorigid metallocene compound belongs to the following formula (I):

wherein:

M is an atom of a transition metal selected from those belonging to group 4; alternatively M is zirconium;

X, equal to or different from each other, is a hydrogen atom, a halogen atom, a R, OR, OR′O, OSO₂CF₃, OCOR, SR, NR₂ or PR₂ group wherein R is a linear or branched, saturated or unsaturated C₁-C₂₀-alkyl, C₃-C₂₀-cycloalkyl, C₆-C₂₀-aryl, C₇-C₂₀-alkylaryl or C₇-C₂₀-arylalkyl radical, optionally containing heteroatoms belonging to groups 13-17 of the Periodic Table of the Elements; and R′ is a C₁-C₂₀-alkylidene, C₆-C₂₀-arylidene, C₇-C₂₀-alkylarylidene, or C₇-C₂₀-arylalkylidene radical; alternatively X is a hydrogen atom, a halogen atom, a OR′O or R group; alternatively X is chlorine or a methyl radical;

R¹, R², R⁵, R⁶, R⁷, R⁸ and R⁹, equal to or different from each other, are hydrogen atoms, or linear or branched, saturated or unsaturated C₁-C₂₀-alkyl, C₃-C₂₀-cycloalkyl, C₆-C₂₀-aryl, C₇-C₂₀-alkylaryl or C₇-C₂₀-arylalkyl radicals, optionally containing heteroatoms belonging to groups 13-17 of the Periodic Table of the Elements; in some embodiments, R⁵ and R⁶, and/or R⁸ and R⁹ form a saturated or unsaturated, 5 or 6 membered rings; in some embodiments, the ring bears C₁-C₂₀ alkyl radicals as substituents; with the proviso that at least one of R⁶ or R⁷ is a linear or branched, saturated or unsaturated C₁-C₂₀-alkyl radical, optionally containing heteroatoms belonging to groups 13-17 of the Periodic Table of the Elements; alternatively a C₁-C₁₀-alkyl radical;

R³ and R⁴, equal to or different from each other, are linear or branched, saturated or unsaturated C₁-C₂₀-alkyl radicals, optionally containing heteroatoms belonging to groups 13-17 of the Periodic Table of the Elements; alternatively R³ and R⁴ equal to or different from each other are C₁-C₁₀-alkyl radicals; alternatively R³ is a methyl, or ethyl radical; and R⁴ is a methyl, ethyl or isopropyl radical.

In some embodiments, the compounds of formula (I) have formula (Ia):

wherein:

M, X, R¹, R², R⁵, R⁶, R⁸ and R⁹ are as described above;

R³ is a linear or branched, saturated or unsaturated C₁-C₂₀-alkyl radical, optionally containing heteroatoms belonging to groups 13-17 of the Periodic Table of the Elements; alternatively R³ is a C₁-C₁₀-alkyl radical; alternatively R³ is a methyl, or ethyl radical.

In some embodiments, the metallocene compounds are selected from the group consisting of dimethylsilyl{(2,4,7-trimethyl-1-indenyl)-7-(2,5-dimethyl-cyclopenta[1,2-b:4,3-b′]-dithiophene)} zirconium dichloride; dimethylsilanediyl{(1-(2,4,7-trimethylindenyl)-7-(2,5-dimethyl-cyclopenta[1,2-b:4,3-b′]-dithiophene)}Zirconium dichloride and dimethylsilanediyl{(1-(2,4,7-trimethylindenyl)-7-(2,5-dimethyl-cyclopenta[1,2-b: 4,3-b ′]-dithiophene)}zirconium dimethyl.

In some embodiments, the alumoxanes are selected from the group consisting of methylalumoxane (MAO), tetra-(isobutyl)alumoxane (TIBAO), tetra-(2,4,4-trimethyl-pentyl)alumoxane (TIOAO), tetra-(2,3-dimethylbutyl)alumoxane (TDMBAO) and tetra-(2,3,3-trimethylbutyl)alumoxane (TTMBAO).

In some embodiments, the compounds capable of forming an alkylmetallocene cation are compounds of formula D⁺E⁻, wherein D⁺ is a Bronsted acid, able to donate a proton and react irreversibly with a substituent X of the metallocene of formula (I) and E⁻ is a compatible anion, which is able to stabilize the active catalytic species originating from the reaction of the two compounds and sufficiently labile to be able to be removed by an olefinic monomer. In some embodiments, the anion E⁻ is made from or contains one or more boron atoms.

In some embodiments, the organo aluminum compound is selected from the group consisting of trimethylaluminum (TMA), triisobutylaluminum (TIBA), tris(2,4,4-trimethyl-pentyl)aluminum (TIOA), tris(2,3-dimethylbutyl)aluminum (TDMBA) and tris(2,3,3-trimethylbutyl)aluminum (TTMBA).

In some embodiments, the catalyst system and polymerization processes employing the catalyst system are as described in Patent Cooperation Treaty Publication Nos. WO2004099269 and WO2009000637.

In some embodiments, the present butene-1 polymer is prepared directly in polymerization.

In some embodiments, the polymerization process is carried out in liquid phase, optionally in the presence of an inert hydrocarbon solvent, or in gas phase, using fluidized bed or mechanically agitated gas phase reactors.

In some embodiments, the hydrocarbon solvent is aromatic or aliphatic. In some embodiments, the aromatic hydrocarbon solvent is toluene. In some embodiments, the aliphatic hydrocarbon solvent is selected from the group consisting of propane, hexane, heptane, isobutane, cyclohexane, 2,2,4-trimethylpentane, and isododecane.

In some embodiments, the polymerization process is carried out by using liquid butene-t 1 as polymerization medium. In some embodiments, the polymerization temperature is from 20° C. to 150° C., alternatively between 50° C. and 90° C., alternatively from 65° C. to 82° C.

In some embodiments, the concentration of hydrogen in the liquid phase during the polymerization reaction (molar ppm H2/ butene-1 monomer) is from 400 ppm to 950 ppm, alternatively from 450 ppm to 900 ppm.

In some embodiments, the amount of comonomer in the liquid phase, when a copolymer is prepared, is from 0.1% to 2.5% by weight, alternatively from 0.5% to 1.5% by weight, with respect to the total weight of comonomer and butene-1 monomer present in the polymerization reactor. In some embodiments, the comonomer is ethylene.

In some embodiments for hot-melt adhesive applications, the present butene-1 polymer is blended with other materials.

In some embodiments, the present disclosure provides a hot-melt adhesive polyolefin composition made from or containing one or more of the following optional components, in addition to the present butene-1 polymer:

I) at least one additional polymer;

II) at least one resin material different from (I);

III) at least one wax or oil; and

IV) a nucleating agent.

In some embodiments, the additional polymer is selected from the group consisting of amorphous poly-alpha-olefins, thermoplastic polyurethanes, ethylene/(meth)acrylate copolymers, ethylene/vinyl acetate copolymers and mixtures thereof. In some embodiments, the resin material different from (I) is selected from the group consisting of aliphatic hydrocarbon resins, terpene/phenolic resins, polyterpenes, rosins, rosin esters and derivatives thereof and mixtures thereof. In some embodiments, the wax or oil is selected from the group consisting of mineral, paraffinic or naphthenic waxes and oils. In some embodiments, the nucleating agent is selected from the group consisting of isotactic polypropylene, polyethylene, amides, stearamides, and talc.

In some embodiments, the amounts by weight of the optional components, with respect to the total weight of the hot-melt adhesive polyolefin composition, when present and independently from each other are:

from 0.1% to 25%, alternatively from 1% to 25% by weight of I);

from 10% to 75%, alternatively from 10% to 40% by weight of II);

from 0.1% to 50%, alternatively from 1% to 30% by weight of III); and

from 0.01% to 1%, alternatively from 0.1% to 1% by weight of IV).

In some embodiments, the components are added and blended in the molten state with the present butene-1 polymer by polymer processing apparatuses. In some embodiments, the polymer processing apparatuses are mono- or twin screw extruders.

In some embodiments, the hot-melt adhesive compositions are used in paper and packaging industry, furniture manufacture, and the production of nonwoven articles. In some embodiments, the furniture manufacture includes edgebands, softforming applications, and paneling in high moisture environments. In some embodiments, the edgebands are square edges. In some embodiments, the nonwoven articles include disposable diapers. In some embodiments, the butene-1 polymer is used in films or fibers. In some embodiments, the present disclosure provides a butene-1 polymer composition for use as a fluidizer for lubricants.

EXAMPLES

Various embodiments, compositions and methods as provided herein are disclosed below in the following examples. These examples are illustrative only, and are not intended to limit the scope of the invention.

The following analytical methods are used to characterize the polymer compositions.

Thermal properties (melting temperatures and enthalpies)

Determined by Differential Scanning calorimetry (D.S.C.) on a Perkin Elmer DSC-7 instrument, as hereinafter described.

-   -   For the determination of TmII (the melting temperature measured         in the second heating run) a weighed sample (5-10 mg) obtained         from the polymerization was sealed into an aluminum pan and         heated at 200° C. with a scanning speed corresponding to 10°         C/minute. The sample was kept at 200° C. for 5 minutes to allow         a complete melting of the crystallites, thereby cancelling the         thermal history of the sample. Successively, after cooling to         −20° C. with a scanning speed corresponding to 10° C/minute, the         peak temperature was taken as the crystallization temperature         (Tc). After standing for 5 minutes at −20° C., the sample was         heated for a second time at 200° C. with a scanning speed         corresponding to 10° C/min. In this second heating run, the peak         temperature measured was taken as (TmII). If more than one peak         was present, the highest (most intense) peak was taken as TmII.         The area under the peak (or peaks) was taken as global melting         enthalpy (DH TmII).     -   The melting enthalpy and the melting temperature were also         measured after aging (without cancelling the thermal history) as         follows by using Differential Scanning calorimetry (D. S.C.) on         a Perkin Elmer DSC-7 instrument. A weighed sample (5-10 mg)         obtained from the polymerization was sealed into an aluminum pan         and heated at 200° C. with a scanning speed corresponding to 10°         C/minute. The sample was kept at 200° C. for 5 minutes to allow         a complete melting of the crystallites. The sample was then         stored for 10 days at room temperature. After 10 days the sample         was subjected to DSC, cooled to -20° C., and then the sample was         heated at 200° C. with a scanning speed corresponding to 10°         C./min. In this heating run, the peak temperature was taken as         the melting temperature (TmI). If more than one peak was         present, the highest (most intense) peak was taken as TmI. The         area under the peak (or peaks) was taken as global melting         enthalpy after 10 days (DH TmI).

MFR

Determined according to norm ISO 1133 with a load of 2.16 kg at 190° C. (standard die).

Intrinsic Viscosity

Determined according to norm ASTM D 2857 in tetrahydronaphthalene at 135° C.

Density

The density of samples was measured according to ISO 1183-1 (ISO 1183-1 method A “Methods for determining the density of non-cellular plastics—Part 1: Immersion method, liquid pyknometer method and titration method”; Method A: Immersion method, for solid plastics (except for powders) in void-free form). Test specimens were taken from compression molded plaques conditioned for 10 days before carrying out the density measure.

Comonomer Contents

Comonomer contents were determined via FT-IR.

The spectrum of a pressed film of the polymer was recorded in absorbance vs. wavenumbers (cm⁻¹). The following measurements were used to calculate the ethylene content:

-   a) area (A_(t)) of the combination absorption bands between 4482 and     3950 cm⁻¹ which is used for spectrometric normalization of film     thickness. -   b) factor of subtraction (FCR_(C2)) of the digital subtraction     between the spectrum of the polymer sample and the absorption band     due to the sequences BEE and BEB (B: butene-1 units, E: ethylene     units) of the methylenic groups (CH₂ rocking vibration). -   c) Area (A_(C2,block)) of the residual band after subtraction of the     C₂PB spectrum, which comes from the sequences EEE of the methylenic     groups (CH₂ rocking vibration).

Aparatus

A Fourier Transform Infrared spectrometer (FTIR) was used.

A hydraulic press with platens heatable to 200° C. (Carver or equivalent) was used.

Method

Calibration of (BEB+BEE) Sequences

A calibration straight line was obtained by plotting % (BEB+BEE)wt vs. FCR_(C2)/A_(t). The slope G_(r) and the intercept I_(r) were calculated from a linear regression.

Calibration of EEE Sequences

A calibration straight line was obtained by plotting %(EEE)wt vs. A_(C2,block)/A_(t). The slope G_(H) and the intercept I_(H) were calculated from a linear regression.

Sample Preparation

Using a hydraulic press, a thick sheet was obtained by pressing about 1.5 g of sample between two aluminum foils. If homogeneity was in question, a minimum of two pressing operations were performed. A small portion was cut from the sheet to mold a film. The film thickness ranged between 0.1-0.3 mm.

The pressing temperature was 140±10° C.

The IR spectrum of the sample film was collected as soon as the sample was molded.

Procedure

The instrument data acquisition parameters were as follows:

-   Purge time: 30 seconds minimum. -   Collect time: 3 minutes minimum. -   Apodization: Happ-Genzel. -   Resolution: 2 cm⁻¹. -   Collect the IR spectrum of the sample vs. an air background.

Calculation

Calculate the concentration by weight of the BEE+BEB sequences of ethylene units:

${\%\left( {{BEE} + {BEB}} \right){wt}} = {{G_{r} \cdot \frac{{FCR}_{C\; 2}}{A_{t}}} + I_{r}}$

Calculate the residual area (AC2, block) after the subtraction described above, using a baseline between the shoulders of the residual band.

Calculate the concentration by weight of the EEE sequences of ethylene units:

${\%({EEE}){wt}} = {{G_{H} \cdot \frac{A_{{C\; 2},{block}}}{A_{t}}} + I_{H}}$

Calculate the total amount of ethylene percent by weight:

% C2wt=[%(BEE+BEB)wt+%(EEE)wt]

NMR Analysis of Chain Structure

¹³C NMR spectra were acquired on a Bruker AV-600 spectrometer equipped with cryo-probe, operating at 150.91 MHz in the Fourier transform mode at 120° C.

The peak of the T_(f)36 carbon (nomenclature according to C. J. Carman, R. A. Harrington and C. E. Wilkes, Macromolecules, 10, 3, 536 (1977)) was used as an internal reference at 37.24 ppm. The samples were dissolved in 1,1,2,2-tetrachloroethane-d2 at 120° C. with an 8% wt/v concentration. Each spectrum was acquired with a 90° pulse, 15 seconds of delay between pulses and CPD to remove ¹H-¹³C coupling. About 512 transients were stored in 32K data points using a spectral window of 9000 Hz.

The assignments of the spectra, the evaluation of triad distribution and the composition were made according to Kakugo [M. Kakugo, Y. Naito, K. Mizunuma and T. Miyatake, Macromolecules, 16, 4, 1160 (1982)] and Randall [J. C. Randall, Macromol. Chem Phys., C30, 211 (1989)] using the following:

BBB=100 (T _(ββ))/S=I5

BBE=100T _(βδ) /S=I4

EBE=100 P _(δδ) /S=I14

EB=100 S _(ββ) /S=I13

BEE=100 S _(αδ) /S=I7

EEE=100(0.25 S _(γδ)+0.5 S _(δδ))/S=0.25 I9+0.5I10

Area Chemical Shift Assignments Sequence 1 40.40-40.14 Sαα BBBB 2 39.64 Tδδ EBE 39-76-39.52 Sαα BBBE 3 39.09 Sαα EBBE 4 37.27 Tβδ BBE 5 35.20-34.88 Tββ BBB 6 34.88-34.49 Sαγ BBEB + BEBE 7 34.49-34.00 Sαδ EBEE + BBEE 8 30.91 Sγγ BEEB 9 30.42 Sγδ BEEE 10 29.90 Sδδ EEE 11 27.73-26.84 Sβδ + 2B₂ BBB + BBE EBEE + BBEE 12 26.70 2B₂ EBE 13 24.54-24.24 Sββ BEB 14 11.22 Pδδ EBE 15 11.05 Pβδ BBE 16 10.81 Pββ BBB

To a first approximation, the mmmm was calculated using 2B2 carbons as follows:

Area Chemical shift assignments B1 28.2-7.45 mmmm B2 27.45-26.30 mmmm = B₁ * 100/(B₁ + B₂ − 2 * A₄ − A₇ − A₁₄)

Mw/Mn and Mz Ddetermination by GPC

Measured by way of Gel Permeation Chromatography (GPC) in 1,2,4-trichlorobenzene (TCB). Molecular weight parameters (Mn, Mw, Mz) and molecular weight distributions Mw/Mn for the samples were measured by using a GPC-IR apparatus by PolymerChar, which was equipped with a column set of four PLgel Olexis mixed-bed (Polymer Laboratories) and an IR5 infrared detector (PolymerChar). The dimensions of the columns were 300×7.5 mm and their particle size was 13 μm. The mobile phase flow rate was kept at 1.0 mL/min. The measurements were carried out at 150° C. Solution concentrations were 2.0 mg/mL (at 150° C.) and 0.3 g/L of 2,6-di-tert-butyl-p-cresol were added to prevent degradation. For GPC calculation, a universal calibration curve was obtained using 12 polystyrene (PS) reference samples supplied by PolymerChar (peak molecular weights ranging from 266 to 1220000). A third-order polynomial fit was used to interpolate the experimental data and obtain the relevant calibration curve. Data acquisition and processing were done by using Empower 3 (Waters). The Mark-Houwink relationship was used to determine the molecular weight distribution and the relevant average molecular weights: the K values were K_(PS)=1.21×10⁻⁴ dL/g and K_(PB)=1.78×10⁻⁴ dL/g for PS and polybutene (PB) respectively, while the Mark-Houwink exponents α=0.706 for PS and α=0.725 for PB were used.

For butene/ethylene copolymers, the composition of each sample was assumed constant in the whole range of molecular weight and the K value of the Mark-Houwink relationship was calculated using a linear combination as reported below:

K _(EB) =x _(E) K _(PE) +x _(B) K _(PB)

where K_(EB) is the constant of the copolymer, K_(PE)(4.06×10⁻⁴, dL/g) and K_(PB) (1.78×10⁻⁴ dL/g) are the constants of polyethylene (PE) and PB, x_(E) and x_(B) are the ethylene and the butene weight relative amount with x_(E)+x_(B)=1. The Mark-Houwink exponents α=0.725 was used for the butene/ethylene copolymers independently on the composition. End processing data treatment was fixed for the samples to include fractions up at 1000 in terms of molecular weight equivalent. Fractions below 1000 were investigated via GC.

Fractions Soluble and Insoluble in Xylene at 0° C. (XS-0° C.)

2.5 g of polymer composition and 250 cm³ of o-xylene were introduced into a glass flask equipped with a refrigerator and a magnetic stirrer. The temperature was raised in 30 minutes up to the boiling point of the solvent. The obtained clear solution was then kept under reflux and stirring for further 30 minutes. The closed flask was then cooled to 100° C. in air for 10 to 15 minutes under stirring and then kept for 30 minutes in thermostatic water bath at 0° C. for 60 minutes. The formed solid was filtered on quick filtering paper at 0° C. 100 cm³ of the filtered liquid was poured in a pre-weighed aluminum container which was heated on a heating plate under nitrogen flow, to remove the solvent by evaporation. The percent by weight of polymer soluble (Xylene Solubles at 0° C.=XS 0° C.) was calculated from the average weight of the residues. The insoluble fraction in o-xylene at 0° C. (xylene Insolubles at 0° C. =XI % 0° C.) was:

XI%0° C.=100−XS%0° C.

Determination of X-Ray Crystallinity

The X-ray crystallinity was measured with an X-ray Diffraction Powder Diffractometer (XDPD) that uses the Cu-Kα1 radiation with fixed slits and able to collect spectra between diffraction angle 2Φ=5° and 2Φ=35° with step of 0.1° every 6 seconds.

The samples were diskettes of about 1.5-2.5 mm of thickness and 2.5-4.0 cm of diameter made by compression molding. The diskettes were aged at room temperature (23° C.) for 96 hours.

After this preparation the specimen was inserted in the XDPD sample holder. The XRPD instrument was set to collect the XRPD spectrum of the sample from diffraction angle 2Φ=5° to 2Φ=35° with steps of 0.1° by using counting time of 6 seconds, and at the end the final spectrum was collected.

Ta was defined as the total area between the spectrum profile and the baseline expressed in counts/sec·2Φ. Aa was defined as the total amorphous area expressed in counts/sec·2Φ. Ca was defined as the total crystalline area expressed in counts/sec·2Φ.

The spectrum or diffraction pattern was analyzed in the following steps:

1) define a linear baseline for the whole spectrum and calculate the total area (Ta) between the spectrum profile and the baseline;

2) define an amorphous profile, along the whole spectrum, that separate , the amorphous regions from the crystalline ones according to the two phase model;

3) calculate the amorphous area (Aa) as the area between the amorphous profile and the baseline;

4) calculate the crystalline area (Ca) as the area between the spectrum profile and the amorphous profile as Ca=Ta−Aa; and

5) calculate the degree of crystallinity (% Cr) of the sample using the formula:

% Cr=100×Ca/Ta

Flexural Modulus

According to norm ISO 178, measured 10 days after molding.

Shore D

According to norm ISO 868, measured 10 days after molding.

Tensile Stress and Elongation at Break

According to norm ISO 527 on compression molded plaques, measured 10 days after molding.

Glass Transition Temperature Via DMTA (Dynamic Mechanical Thermal Analysis)

Molded specimens of 76 mm by 13 mm by 1 mm were fixed to a DMTA machine for tensile stress. The frequency of the tension was fixed at 1 Hz. The DMTA translated the elastic response of the specimen starting from −100° C. to 130° C. The elastic response was plotted versus temperature. The elastic modulus for a viscoelastic material was defined as E=E′+iE″. In some instances, the DMTA split the two components E′ and E″ by resonance and plotted E′ vs temperature and E′/E″=tan (δ) vs temperature.

The glass transition temperature Tg was assumed to be the temperature at the maximum of the curve E′/E″=tan (δ) vs temperature.

Yellowness Index

Determined accordingly to ASTM D1925.

Examples 1-3 and Comparative Example 1

Preparation of the Metallocene Catalyst (A-1)

Dimethylsilyl{(2,4,7-trimethyl-1-indenyl)-7-(2,5-dimethyl-cyclopenta[1,2-b:4,3-b′]-dithiophene)} zirconium dichloride (A-1) was prepared according to Example 32 of Patent Cooperation Treaty Publication No. WO0147939.

Preparation of the Catalytic Solution

Under nitrogen atmosphere, 8.1 L of a solution of 4.5% wt/v of TIBA in isododecane (1.84 mol of TIBA) and 760 mL of a solution 30% wt/wt of MAO in toluene (3.65 moles of MAO) were loaded in a 20 L jacketed glass reactor equipped with an anchor stirrer and allowed to react at room temperature for about 1 hour under stirring.

After this time, the metallocene A-1 (1.6 g, 2.75 mmol) was added and dissolved under stirring for about 30 minutes.

The final solution was discharged from the reactor into a cylinder through a filter to remove solid residues (if any).

The composition of the solution was as follows:

Al Zr Al/Zr Metallocene g/L % w mol ratio Conc. mg/L 16.7 0.028 1996 181

Polymerization

The polymerization was carried out continuously in a pilot plant including a stirred reactor in which liquid butene-1 constituted the liquid medium.

The polymerization conditions are reported in Table 1.

TABLE 1 Operative conditions Ex. 1 Ex. 2 Ex. 3 Temperature (° C.) 75 75 75 H₂ in liquid phase (ppm mol) 694 694 699 C₂H₄ in liquid phase (weight %) 1.29 0.93 0.87 Mileage (kg/gMe) 1682 1800 1781 Note: C₂H₄ = ethylene; kg/gMe = kilograms of polymer per gram of metallocene catalyst (A-1); Split = amount of polymer produced inthe concerned reactor.

In Table 2 the properties of the final products are specified.

Table 2 reports also the properties of the butene-1 polymer taken as comparison (Comparative Example 1), which was a commercial copolymer containing 6.8% by mole of ethylene, prepared with a Ziegler-Natta catalyst and subsequently subjected to a peroxide treatment.

TABLE 2 Ex. 1 Ex. 2 Ex. 3 Comp. 1 MFR 190° 2.16 Kg g/10 min 45 56 37 36 Intrinsic Viscosity dl/g 0.86 0.8 0.84 1.01 C₂H₄ IR mol % 7.3 5.6 4.7 6.8 TmII ° C. 64.4 73 74.8 87 DH TmII J/g 0.6 7.5 3.0 14.5 TmI ° C. 37-55-64.5 37-60-73-85 39-62-75-88 92 DH TmI J/g 36 37 41.8 38.7 X-Ray crystallinity % 26 29 32 38 Xylene Soluble at 0° C. % 99.7 99.6 99.7 47.6 Mw g/mol 135570 131228 143923 131306 Mn g/mol 59634 61506 66768 28914 Mw/Mn 2.3 2.1 2.2 4.5 Mz g/mol 227843 217297 241167 249748 Density g/cm3 0.890 0.893 0.898 0.897 Flexural Modulus MPa 134 155 180 155 Strength at Break MPa 22.1 29.9 32.9 28.1 Elongation at Break % 485 471 503 505 Hardness Shore D D 31.6 41.3 42.3 57 Glass transition ° C. −22 −22 −21 −16 temperature 

What is claimed is:
 1. A butene-1 polymer having: a) a MFR value of from 20 to less than 100 g/10 min., measured according to ISO 1133 at 190° C. with a load of 2.16 kg; b) an intrinsic viscosity (IV) measured in tetrahydronaphthalene (THN) at 135° C. equal to lower than 0.95 dl/g; c) a Mw/Mn value, where Mw is the weight average molar mass and Mn is the number average molar mass, both measured by GPC (Gel Permeation Chromatography), equal to or lower than 3.5 and a lower limit of 1.5; d) a Mz value of 180,000 g/mol or higher; and e) optionally, a comonomer content of up to 10% by mole.
 2. The butene-1 polymer of claim 1, having DH TmII values of 25 J/g or less, measured with a scanning speed corresponding to 10° C./min.
 3. The butene-1 polymer composition of claim 1, having a Mw equal to or greater than 90.000 g/mol.
 4. The butene-1 polymer of claim 1, having a glass transition temperature of −18° C. or less.
 5. A process for preparing the butene-1 polymer of claim 1, comprising: polymerizing butene-1 monomer optionally, with one or more comonomers in the presence of a metallocene catalyst obtainable by contacting: a stereorigid metallocene compound; an alumoxane or a compound capable of forming an alkyl metallocene cation; and, optionally, an organo aluminum compound.
 6. A manufactured article comprising: the butene-1 polymer of claim
 1. 7. The manufactured article of claim 6 being films or fibers.
 8. A hot-melt adhesive composition comprising: the butene-1 polymer composition of claim
 1. 